Optical glass

ABSTRACT

The present invention provides optical glasses containing Bi2O3 in which the optical glasses have at least one of the properties of being substantially free from opacification and being substantially devitrified within the glass body during reheating steps in production processes, superior chemical durability, and free from black coloring. The optical glass has a refractive index (nd) of no less than 1.75 and an Abbe number (νd) of no less than 10 as optical constants. The optical glass contains Bi2O3 in a content from no less than 10% by weight to less than 90% by weight, and has at least one of the properties of being substantially free from opacification and being substantially devitrified within the glass body under the conditions of a reheating test (a).

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to optical glasses containing bismuth oxide, more particularly to optical glasses having at least one of the properties of being free from opacification and being devitrified in a glass body under such conditions as press-molding, including precision presses and reheat presses as well as reheat tests thereof.

2. Related Art

In recent years equipments or instruments, equipped with optical systems, have been highly integrated and sophisticated, which leading to more and more demands for the optical systems in terms of high accuracy, lightweight and miniaturization, thus the optical systems have been mainly designed using aspheric lenses formed of high index/high dispersion glasses in order to reduce the number of lenses.

It is expensive and non-efficient in particular to produce aspheric lenses by way of grinding or polishing processes; therefore, the aspheric lenses are presently produced by lower cost mass-production processes without the grinding or polishing processes such that gobs or glass blocks are cut and grinded to form a preform material, the preform material is heated and softened then is pressure-molded by use of a mold having a highly precise surface.

In order to attain the object to mass-produce the aspheric lenses with lower cost, it is necessary to investigate various conditions so as to satisfy items (i) to (iii) below:

(i) the glass is free from devitrification i.e. maintains transparency under reheating conditions, for example, of reheating-pressing processes for softening gobs or glass blocks by heating thereof;

(ii) the glass has superior chemical durability such that particular control is unnecessary in handling thereof after the polishing step; and

(iii) the temperature at mold-pressing step is as low as possible, so that molds for the mold-pressing can be far from surface oxidation and thus be repeatedly usable (there exists a relation between upper temperatures at mold-pressing and transition temperatures; the progress of the surface oxidation may be slower as these temperatures being lower).

With respect to (i) described above, the glasses based on TiO₂ or Nb₂O₅ containing SiO₂ or B₂O₃ as a former tend to exhibit relatively higher transition temperatures or higher glass yield points. Accordingly, these glasses are inappropriate for mass production, since crystals are likely to deposit at reheating steps at producing aspheric lenses, which causing problems such as lowering of process yield.

On the other hand, Patent Literatures 1 and 2 disclose glasses based on P₂O₅ utilized as precision-press materials. These materials may be softened and press-molded at temperatures lower than those of conventional SiO₂ glasses. However, these glasses still exhibit higher glass transition temperatures, so that the glasses react with surfaces of mold materials, consequently optical parts come to difficult to reproduce the surface accuracy at the transferred surfaces through the precision-molding processes, and also the surfaces of mold materials tend to be injured. Furthermore, these glasses are likely to cause the devitrification due to basic components of P₂O₅, TiO₂, Nb₂O₅ or WO₃ through the reheating step, and also are relatively difficult to undergo precision press-molding due to problems such as possible fusion with molds or their clacks.

In addition, Patent Literature 3 discloses a glass containing Bi₂O₃ as a basic component; however, the refractive index and the dispersion are insufficient and also the glass transition point is higher. Furthermore, there exist such problems as the glass tends to display considerable opacification or to color into black at the reheating step in producing processes of the aspheric lenses or at reheating tests corresponding to reheat presses.

-   Patent Literature 1: Japanese Unexamined Patent Publication No.     07-97234 -   Patent Literature 2: Japanese Unexamined Patent Publication No.     2002-173336 -   Patent Literature 3: Japanese Unexamined Patent Publication No.     09-20530

The present invention has been made in light of the objects described above; that is, the present invention provides optical glasses containing bismuth oxide in which the optical glasses are having at least one of the properties of being free from opacification and being devitrified within glass body at the reheating step in producing processes of the aspheric lenses or at the reheating tests corresponding to the reheat presses, and also optical glasses with superior chemical durability and free from coloring into black.

SUMMARY OF THE INVENTION

In order to solve the problems described above, we have investigated vigorously and found that a desirable glass can be obtained with lower production costs that exhibits a high index/high dispersion such as 1.75 or more of refractive index (n_(d)) and from 15 to 35 of Abbe number (ν_(d)) as optical constants, and has a glass transition point (Tg) of no more than 550 degrees C., with at least one of the characteristics of being free from opacification and being devitrified within the glass body during the reheating step in the production processes of the aspheric lenses or during the reheating test corresponding to reheat presses, and also being free from black coloring, such that the present invention has been completed. More specifically, the present invention provided as described below.

According to a first aspect of the present invention, an optical glass of the present invention has a refractive index (n_(d)) of no less than 1.75 and an Abbe number (ν_(d)) of no less than 10 in terms of the optical constants, in which the Bi₂O₃ content is from no less than 10% by weight to no more than 90% by weight, and has at least one of the characteristics of being substantially free from opacification and/or being devitrified within glass body under the condition of reheating test (a) shown below:

whereby, a test piece of 15 mm by 15 mm by 30 mm is reheated such that the test piece is heated from room temperature to a temperature of 80 degrees C. higher than its transition temperature (Tg) for a period of 150 minutes, maintained for 30 minutes at the temperature of 80 degrees C. higher than the glass transition temperature (Tg) of the optical glass, allowed to cool to an ambient temperature, and finally observed visually after polishing the opposing two sides of the test piece to thickness of 10 mm.

The optical glass according to the present invention may have at least one of the characteristics of being free from opacification and being devitrified within glass body under the condition of reheating test (a), thus an optical glass may be provided which has at least one of the properties of hardly opacifying and being devitrified even during the reheating step in the production process thereof.

In a second aspect of the optical glass as described in the first aspect of the present invention, the transmissivity loss is no more than 5% at respective wavelengths of visible region in the reheating test (b) under the following conditions:

whereby, a two side-polished test piece having a thickness of 10 mm is heated from room temperature to a yield point by increasing the temperature at a rate of 6.5 degrees C. per second under a non-oxidizing atmosphere, being maintained at the yield point for 300 seconds, and lowering the temperature to 220 degrees C. by decreasing the temperature at a rate of 2.4 degrees C. per second, and thereafter measuring the transmissivity of the test piece to determine the transmissivity of before and after the test.

The optical glass according to the present invention exhibits the transmissivity loss of no more than 5% at respective wavelengths of the visible region in the reheating test (b), thus an optical glass may be provided which hardly turns black in color even during reheating steps in production process thereof. The reason the glass turns black in color is that the component of Bi₂O₃ turns into metal bismuth by action of non-oxidative gas when the glass material undergoes precision press-molding to produce an optical glass and the like. The term “respective wavelengths of visible region” as used herein means the wavelengths of 360 nm to 800 nm. The non-oxidative gas is preferably nitrogen gas, for example. The term “transmissivity loss” refers to the loss of transmissivity that is caused in the tested test piece compared to the pre-test test piece through the reheating test (b).

In a third aspect of the optical glass as described in any one of aspects one through three of the present invention, the value, calculated by dividing the transmissivity of the test piece after the reheating test (a) by the transmissivity of the test piece before the reheating test using a radiation (D ray) of wavelength 587.56 nm, is no less than 0.95.

In a fourth aspect of the optical glass as described in any one of aspects one through three of the present invention, the difference in a wavelength λ₇₀ of the test piece before the reheating test (a) and a wavelength λ₇₀ after the reheating test is no more than 20 nm, where the “λ₇₀” refers to the wavelength at which the transmissivity being 70%.

According to the third and fourth aspects of the present invention, an optical glass may be easily provided that exhibits less transmissivity variation even at the reheating step in the production process thereof, since the value calculated from the transmissivities after and before the reheating test (a) is no less than 0.95, or the difference of λ₇₀ is no more than 20 nm between after and before the reheating test (a).

In a fifth aspect of the optical glass as described in any one of aspects one through four of the present invention, the crystal deposit condition of the test piece after the reheating test (a) displays an internal quality of a first or second grade and A or B grade with respect to the evaluation which is in accordance with a measuring method for inclusion JOGIS13-1994.

According to this aspect of the present invention, an optical glass may be easily provided with less foreign substances even during the reheating step in the production process thereof, by virtue of the internal quality of the first or second grade and A or B grade even after the reheating test (a) by the evaluation which is in accordance with the method of determining foreign substances JOGIS13-1994.

Concerning the description “internal quality of the first or second grade and A or B grade”, the first grade indicates that the total cross section of foreign substances JOGIS13-1994 is less than 0.03 mm², and the second grade indicates that the total cross section is from no less than 0.03 mm² to no more than 0.1 mm² on the basis of 100 ml. The A grade indicates that the total number of the foreign substances is less than 10, and the B grade indicates from no less than 10 to less than 100 on the basis of 100 ml.

In a sixth aspect of the optical glass as described in any one of aspects one through five of the present invention, the transition temperature (Tg) of the glass is no more than 550 degrees C.

In accordance with this aspect, the temperature at mold pressing may be set at a lower temperature since the transition temperature (Tg) of the glass is no more than 550 degrees C. Accordingly, the reactivity between the glass and molds can be reduced, thus the transmissivity degradation may be easily suppressed, and at least one of the properties of opacification and vitrification of the glass may be easily prevented.

In a seventh aspect of the optical glass as described in any one of aspects one through six of the present invention the content of SiO₂ is lower than the content of B₂O₃, the total content of SiO₂+B₂O₃ is from no less than 1% by weight to no more than 60% by weight; and the total content of TiO₂+Nb₂O₅+WO₃+RO+Rn₂O is no more than 60% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.

In a eighth aspect of the optical glass as described in any one of aspects one through six of the present invention, the content of SiO₂ is lower than the content of B₂O₃, the total content of SiO₂+B₂O₃ is from no less than 1% to no more than 60% by weight; and the total content of TiO₂+Nb₂O₅+WO₃+RO+Rn₂O is from no less than 0.1% by weight to no more than 55% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.

In a ninth aspect of the optical glass as described in any one of aspects one through eight of the present invention, the content of SiO₂ is lower than the content of B₂O₃, the total content of SiO₂+B₂O₃ is from no less than 1% by weight to no more than 60% by weight; and the total content of RO+Rn₂O is from no less than 0.1% by weight to no more than 60% by weight, in which R represents one or more elements selected from the group including Zn, Ba, Sr, Ca and Mg; Rn represents one or more elements selected from the group including Li, Na, K and Cs.

According to the aspects seven to nine of the present invention, SiO₂+B₂O₃ and RO component+Rn₂O component may stabilize the glass and also suppress transmissivity degradation in the reheating test (b). Accordingly, the optical glasses produced in these compositions may easily avoid transmissivity degradation through the reheating test.

In a tenth aspect of the optical glass as described in any one of aspects one through nine of the present invention, the content of SiO₂ is lower than the content of B₂O₃, the total content of SiO₂+B₂O₃ is from no less than 1% by weight to no more than 60% by weight, and the total content of Ln₂O₃+RO+Rn₂O is from no less than 0.5% by weight to no more than 50% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs; Ln represents one or more elements selected from the group consisting of La, Gd, Y, Ce, Eu, Dy, Yb and Lu.

According to this aspect of the present invention, the total content of Ln₂O₃+RO+Rn₂O within the range described above may lead to easy stabilization of the glass.

In a eleventh aspect of the optical glass as described in any one of aspects one through ten of the present invention, the content of MgO is less than 4% by weight, and the total content of TiO₂+Nb₂O₅+WO₃+Ln₂O₃ is no more than 10% by weight, in which Ln represents one or more elements selected from the group consisting of La, Gd, Y, Ce, Eu, Dy, Yb and Lu.

According to this aspect of the present invention, the total content of TiO₂+Nb₂O₅+WO₃+Ln₂O₃ within the range described above may suppress the tendency to increase devitrification which is induced by the component MgO during the reheating test.

In a twelfth aspect of the optical glass as described in the eleventh aspect of the present invention, the content of Rn₂O is 0% by weight to 1.5% by weight, in which Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.

The alkaline metal components may be remarkably effective in stabilizing glasses and to lowering temperatures corresponding to thermal properties; therefore, the content of Rn₂O within the range described above may bring about easy control of the glass water-resistance. Furthermore, the deterioration of moldability that is induced by possible alkaline elution at precision press-molding steps may be easily avoided.

In a thirteenth aspect of the optical glass as described in any one of aspects one through twelve of the present invention, the total content of Bi₂O₃+SiO₂+Al₂O₃+ZrO₂ is no less than 75% by weight.

According to this aspect of the present invention, the total content of Bi₂O₃+SiO₂+Al₂O₃+ZrO₂ within the range described above may allow control of improvement of chemical durability, along with satisfying the refractive index of the glass. In addition, it may easily suppress coloring during mold-pressing. When a glass is to be produced with superior water resistance in particular, it is effective to raise the content of Bi₂O₃ and SiO₂; and when the acid resistance is to be improved, it is effective to decrease the content of Bi₂O₃ and to increase the content of Al₂O₃ and ZrO₂.

In a fourteenth aspect of the optical glass as described in any one of aspects one through thirteen of the present invention, the weight loss of the glass is no more than 0.2% by weight in terms of chemical durability test based on powder method in accordance with JOGIS06-1996.

According to this aspect of the present invention, the glass may be prevented from turning black in color when the glass undergoes precision press-molding to produce optical glasses and the like since the weight loss of the glass is no more than 0.2% by weight in terms of chemical durability test based on a powder method in accordance with JOGIS06-1996. Furthermore, the resulting glasses may be easily prevented from degradation at rinsing steps or during storage of the optical glasses, and also the transmissivity degradation may be easily prevented after forming lenses.

The term “chemical durability” refers to a decay in durability against glass corrosion induced by water, which may be determined by way of a “Method of Determining Chemical Durability of Optical Glass” JOGIS06-1996 as specified by Japanese Optical Glass Industrial Standards. The method rates samples into 6 steps of class 1 to class 6 from their weight loss on the basis of their weights before and after the test. The glass weight loss of 0.2% corresponds to a water resistance equal to or superior than class 3. In the method, class 1 represents less than 0.05% by weight of the weight loss on the basis of the weights before and after the test, class 2 represents from no less than 0.05% by weight to less than 0.10% by weight, class 3 represents from no less than 0.10% by weight to less than 0.25% by weight, class 4 represents from no less than 0.25% by weight to less than 0.60% by weight, class 5 represents from less than 0.60% by weight to less than 1.10% by weight, and class 6 represents no less than 1.10% by weight.

In a fifteenth aspect of the optical glass as described in any one of aspects one through fourteen of the present invention, the value of (SiO₂+Al₂O₃+ZrO₂)/RO is no less than 0.5.

According to a sixteenth aspect of the present invention, an optical element formed by precision press-molding the optical glass according to any one of aspects one to fifteen.

According to the present invention, an optical element may be easily provided by way of precision press-molding since the optical glass hardly causes devitrification and also hardly colors into black even after reheating thereof.

In a seventeenth aspect of the optical glass as described in any one of aspects one through fifteen of the present invention, the preform is utilized for precision press-molding.

According to the sixteenth aspect of the present invention, an optical element formed by precision press-molding the preform for precision press-molding as described in the seventeenth aspect.

According to the seventeenth and eighteenth aspects of the present invention, the preform may be effectively utilized for precision press-molding since the preform is free from devitrification or coloring even after reheating thereof, thus the optical element may be easily produced by precision press-molding the preform for precision press-molding.

The optical glass according to the present invention may be provided as excellent optical glasses in terms of preform productivity, properties of preform itself, and press-molding property by virtue of employing the constitutional elements described above, furthermore, optical glasses may be easily provided with generally excellent properties including remarkably appropriate press-molding property.

DETAILED DESCRIPTION OF THE INVENTION

The optical glass according the present invention will be explained with respect to specific embodiments below.

Glass Component

The composition range of respective components that constitute the inventive optical glasses will be explained in the following. The respective components are expressed in terms of % by weight. The glass compositions expressed in this specification are entirely on the basis of oxide. The term “on the basis of oxide” means that the contents of the respective components are expressed assuming that the raw materials of the inventive glasses such as oxides and nitrates are entirely turned into oxides through decomposition and the like at the melting step and the total content of resulting oxides is 100% by weight.

Essential and Optional Components

Bi₂O₃ is an essential component in order to attain the object of the present invention since it is effective to stabilize glasses, to achieve high index/high dispersion and to lower glass transition temperatures (Tg). Excessively higher amount of Bi₂O₃, however, tends to degrade glass stability, and excessively lower amount of Bi₂O₃ makes difficult to attain the inventive object. Accordingly, the content of Bi₂O₃ is preferably no less than 10%, more preferably no less than 20% and most preferably no less than 30%, preferably less than 90%, more preferably no more than 85% and most preferably no more than 80%.

B₂O₃ or SiO₂ is an essential component as a glass-forming oxide, and significantly effective for the devitrification and to raise the viscosity at the liquid-phase temperature. The lower-limit content of one of these components or sum of these components is preferably 1%, more preferably 3%, and still more preferably 7%. On the other hand, the upper-limit content thereof is preferably 60%, more preferably 50% and still more preferably 40% in order to achieve desirable refractive indexes.

These two components may exhibit an effect to improve devitrification resistance even when one of these is introduced alone in the glasses, thereby the object of the present invention may be attained. When the ratio SiO₂/B₂O₃ is controlled to less than 1.0 (the content of SiO₂ being less than that of B₂O₃), the devitrification resistance may be further improved within glass body.

When a glass yield point (At) according to the inventive object is to be attained effectively, the upper-limit content of B₂O₃ is preferably defined as 30%, more preferably 25% and most preferably 20%. In addition, the upper-limit content of SiO₂ is preferably defined as 20%, more preferably 15% and most preferably 10%.

Al₂O₃ is an effective component to improve chemical durability; however, excessively higher content thereof tends to deteriorate glass solubility, to increase devitrification, and to raise the glass yield point. Accordingly, the upper-limit content is preferably defined as 20%, more preferably 15% and most preferably 10%.

TiO₂ is an effective optional component in the glasses to raise the refractive index, to contribute to the high dispersion, and to lower the liquid-phase temperature; however, excessively higher content thereof tends to disadvantageously prompt the devitrification. Accordingly, the content is preferably defined as no more than 20%, more preferably no more than 10% and most preferably no more than 5%.

Nb₂O₅ is an effective optional component in the glasses to raise the refractive index, to contribute to the high dispersion and to improve devitrification; however, excessively higher content thereof tends to deteriorate the glass solubility. Accordingly, the content is preferably defined as no more than 20%, more preferably no more than 15% and most preferably no more than 8%.

WO₃ is an effective optional component in the glasses to raise the refractive index, to contribute to the high dispersion and to lower the yield point; however, excessively higher content thereof tends to increase phase-separation in glasses. Accordingly, the content is preferably defined as no more than 15%, more preferably no more than 10%, and most preferably no more than 5%.

Ta₂O₅ is an effective optional component in the glasses to raise the refractive index and to improve to the chemical durability; however, excessively higher content thereof tends to increase phase-separation in the glasses. Accordingly, the upper-limit content is preferably defined as 15%, more preferably 10% and most preferably 5%. Still more preferably, there exists no Ta₂O₅.

ZrO₂ is an optional component effective to improve to the chemical durability; however, excessively higher content thereof tends to promote inclination to the devitrification of the glasses. Preferably, the upper-limit content is defined as 10%, more preferably 5% and most preferably 2%. Still more preferably, there exists no ZrO₂.

As described above, Al₂O₃ and ZrO₂ are effective components for improving the chemical durability; Bi₂O₃ provides an effect to enhance the water resistance. SiO₂ is an essential component as a glass-forming oxide which is significantly effective for the devitrification and for raising the viscosity at the liquid-phase temperature. Accordingly, it is preferred that these components are controlled in a certain range so as to satisfy the devitrification and the chemical durability of the glasses. In addition, the present inventors have found that there is an intimate relation between the transmissivity degradation and the water resistance in precision press-molding products, that is, the enhancement of water resistance or establishment of firm glass construction may significantly contribute to mitigate the transmissivity degradation at precision pressing steps. As such, when the total content of these components is excessively lower, the glass is likely to cause the coloring at heating under non-oxidative atmosphere and also to degrade the devitrification resistance. Accordingly, the lower limit of the total content of Bi₂O₃, SiO₂, Al₂O₃ and ZrO₂ is preferably 65%, more preferably 70% and most preferably 75%.

In addition, the RO component described later is an optional component that may provide mainly an effect to stabilize the glasses; when an optical constant is to be controlled, it may be considered as a reference for the entire composition. That is, when the refractive index to be raised by use of a component such as Bi₂O₃ or to be lowered by use of other components, a portion of the RO component is often substituted by a component. As such, the chemical durability and the glass stability may be properly satisfied by way of setting the total content of SiO₂, Al₂O₃ and ZrO₂ while considering the RO as a reference. Accordingly, the ratio of the total content of SiO₂, Al₂O₃ and ZrO₂ to the RO component is preferably no less than 0.5, more preferably no less than 0.6, and most preferably no less than 0.7.

The RO component, in which R represents one or more elements selected from the group consisting of Zn, Ba, Ca, Mg and Sr, may increase the melting property and the devitrification resistance and to enhance the chemical durability, thus the glasses preferably contain any of these components. Preferably, the glasses contain the RO, in which R represents one or more elements selected from the group consisting of Zn, Ba, Ca, Mg and Sr in a total content of no less than 0.1%, more preferably no less than 5% still more preferably no less than 10%.

ZnO is an effective component to improve to the chemical durability; however, excessively higher content thereof tends to allow the devitrification of the glasses. Accordingly, it is preferred that the upper-limit content is defined as 20%, more preferably 15% and most preferably 10%.

CaO is an effective component to improve to the melting property of the glasses; however, excessively higher content thereof tends to allow the devitrification. Accordingly, it is preferred that the upper-limit content is defined as 20%, more preferably 15% and most preferably 10%.

BaO is an effective component to improve the devitrification and the coloring of the glasses; however, excessively higher content thereof may disturb the refractive index intended by the present development. Accordingly, it is preferred that the upper-limit content is defined as 50%, more preferably 40% and most preferably 35%. The lower-limit content is preferably defined as 0.1%, more preferably 1% and most preferably 3%.

MgO is an effective component to attain the high dispersion of the glasses; however, excessively higher content thereof may promote the occurrence of the devitrification at the reheating test. Accordingly, it is preferred that the upper-limit content is defined as less than 10%, more preferably less than 7% and most preferably less than 4%.

SrO is an effective component to improve the devitrification property of the glasses; however, excessively higher content thereof may make difficult to attain the intended optical constant. Accordingly, it is preferred that the upper-limit content is defined as 50%, more preferably 40% and most preferably 35%.

The Rn₂O component, in which Rn represents one or more elements selected from the group consisting of K, Na, Li and Cs is an effective optional component in the glasses to lower the melting property and the glass yield point; however, excessively higher content thereof may promote the transmissivity degradation at heating under non-oxidative atmosphere. Accordingly, it is preferred that the upper-limit content is defined as 10%, more preferably 5% and most preferably 1.5%.

Li₂O is an effective component in the glasses to improve the melting property and to prevent the occurrence of devitrification at the reheating test; however, excessively higher content thereof may make difficult to take the refractive index intended in the present invention. Accordingly, it is preferred that the upper-limit content is defined as 15%, more preferably 10% and most preferably 5%.

Na₂O is an effective component in the glasses to improve the devitrification property and to prevent the occurrence of devitrification at the reheating test; however, excessively higher content thereof may lower the refractive index. Accordingly, it is preferred that the upper-limit content is defined as 15%, more preferably 10% and most preferably 5%.

K₂O is an effective component in the glasses to improve the devitrification property; however, excessively higher content thereof may make difficult to take the refractive index intended in the present invention. Accordingly, it is preferred that the upper-limit content is defined as 20%, more preferably 15% and most preferably 10%.

Furthermore, in order to improve the devitrification property intended in the present invention, it is preferred that the lower-limit content of RO+Rn₂O is defined as 0.1%, more preferably 5% and most preferably 10%. The upper-limit is preferably defined as 60%, more preferably 55% and most preferably 50%.

TiO₂, Nb₂O₅ and WO₃ are significantly important components to control the optical constant as described above, and these contents are preferably adjusted to certain levels while keeping a relation with RO and/or Rn₂O components. When the total content is excessively higher, the devitrification tends to develop significantly, thus the glass stability may be degraded remarkably. Accordingly, the upper-limit of TiO₂, Nb₂O₅, WO₃, RO and Rn₂O is preferably 60% in terms of their total content, preferably 55% and most preferably 50%. The lower-limit is preferably no less than 0.1%, and 0% is allowable.

When the content of TiO₂, Nb₂O₅ and WO₃ is excessively high as for the total content with Ln₂O₃, the glass stability may be degraded remarkably. Accordingly, the upper-limit of TiO₂, Nb₂O₅, WO₃ and Ln₂O₃ is preferably 60% in terms of their total content, preferably 40% and most preferably 10%.

The components of Y₂O₃, La₂O₃, Gd₂O₃ and Yb₂O₃ are effective in the glasses to enhance the chemical durability, and these components may be added optionally. When the content is excessively higher, the dispersion tents to be deteriorated and the devitrification resistance tends to increase. Accordingly, the upper-limit of these components is preferably defined as 10% in terms of their total content, more preferably 7% and most preferably 0.1%. Still more preferably, there exists no these components.

In addition, it is preferred that the total content of Ln₂O₃, in which Ln represents one or more elements selected from the group consisting of La, Gd, Y, Ce, Eu, Dy, Yb and Lu is controlled within a range considering the relation with the content of RO and/or Rn₂O components. The upper limit of Ln₂O₃, RO and Rn₂O is preferably 50% in terms of their total content, more preferably 48% and most preferably 45%. The lower-limit is preferably 0.5%, more preferably 1% and most preferably 1.5%.

P₂O₅ is a component effective to improve the coloring in the glasses, and the component may be added optionally. Excessively higher content thereof tends to promote phase-separation of the glasses. Accordingly, the upper-limit of the component is preferably defined as 10%, more preferably 5%, and most preferably 1%. Still more preferably, there exists no this component.

Sb₂O₃ may be optionally added for defoaming the melted glasses, and provides the effect sufficiently in a content of no more than 3%.

GeO₂ is an effective component in the glasses to improve the coloring and to enhance the high index/high dispersion, and is added in some cases considering its relatively higher cost. Accordingly, the upper-limit of the component is preferably defined as 20%, more preferably 10% and most preferably 5%. Still more preferably, there exists no this component.

F may affect to enhance the melting property of the glasses, and may optionally be added since it drops the refractive index drastically. Accordingly, the upper-limit of the component is preferably defined as 5%, more preferably 3% and most preferably 1%. Still more preferably, there exists no this component.

Components Non-Desirable to Include

The other components may be added as required provided that the properties of the inventive glasses are not deteriorated. In this regard, components of various transition metals such as V, Cr, Mn, Fe, Co, Ni, Cu, Ag and Mo, except for Ti, induce coloring of the glasses even when included at a small amount individually or in combination thereof, thereby causing radiation absorption at a certain visible wavelength. Accordingly, it is desirable for optical glasses employed at visible wavelengths to contain substantially no these components.

Th component may be included for the purpose of raising the refractive index and stabilizing the glasses, and Cd and Tl components may be included for the purpose of lowering the glass transition temperature (Tg). However, in these years the components of Pb, Th, Cd, Tl and Os are likely to be avoided from their usage in light of harmful chemical substances, and environmental measures are required not only at the production steps of the glasses but also at processing steps and disposal of the produced articles. Accordingly, it is preferred that these components are substantially excluded when the environmental effects are important.

The component of lead requires the environmental measures at producing, processing and disposing of the glasses, resulting in higher cost, thus the lead is to be nothing within the inventive glasses.

As₂O₃ is a component to improve the defoaming property at melting the glasses; however, it requires the environmental measures at producing, processing and disposing of the glasses, thus it is undesirable to include As₂O₃ in the inventive glasses.

In accordance with the present invention, it is preferred that at least one of the following components is included, as indicated:

Bi₂O₃: 10 to less than 90%,

SiO₂: more than 0% to less than 20%,

BaO: 0 to 50%,

B₂O₃: 0 to 30%,

Al₂O₃: 0 to 20%,

TiO₂: 0 to 20%,

Nb₂O₅: 0 to 20%,

WO₃: 0 to 15%,

Ta₂O₅: 0 to 15%,

ZrO₂: 0 to 10%,

ZnO: 0 to 20%,

MgO: 0 to less than 10%,

CaO: 0 to 20%,

SrO: 0 to 50%,

Li₂O: 0 to 15%,

Na₂O: 0 to 15%,

K₂O: 0 to 20%,

Y₂O₃: 0 to 10%,

La₂O₃: 0 to 10%,

Gd₂O₃: 0 to 10%,

Yb₂O₃: 0 to 10%,

P₂O₅: 0 to 10%,

Sb₂O₃: 0 to 3%,

GeO₂: 0 to 20%, and

F: 0 to 5%.

The optical glasses according to the present invention are of high index/high dispersion, and may easily display a glass transition temperature (Tg) of no more than 550 degrees C. Preferable range of the Tg is no more than 530 degrees C., more preferably is no more than 510 degrees C.

Production Method

The optical glasses according to the present invention may be produced by conventional methods of producing optical glasses without limitation, for example, may be produced by the method described below. Each of the raw materials such as oxides, carbonates, nitrates, phosphates, sulfates and fluoride salts is weighed to a predetermined amount and combined uniformly. The combined raw material is poured into a quartz or alumina crucible and is preliminarily melted, then poured into a gold, platinum, platinum alloy, or iridium crucible and melted within a melting furnace at 850 to 1250 degrees C. for 1 to 10 hours. Then the material is mixed and homogenized, followed by cooling to an appropriate temperature and casting within a mold etc. thereby to produce the glass.

Reheating Test

The glasses free from devitrification within the glass body or those having a transmissivity loss of no more than 5% in the reheating test (a) or (b) may expand freedom in optical design. Furthermore, the chromatic aberration, which conventionally having been reduced by use of complicated processing of lens shape represented by aspheric processing or by way of increasing the number of lenses, may be effectively reduced without such complicated processing of lens shape or increasing the number of lenses, and also the reheating treatment represented by reheating press processing may be carried out easily, thereby the production cost of the optical elements may be saved.

The reheating test (a) is carried out as following: a test piece of a prismatic shape glass sample of 15 mm by 15 mm by 30 mm is set on a refractory body and disposed in an electric furnace, then is reheated. The heating cycle is such that the sample is heated from the ambient temperature to the temperature 80 degrees C. higher than the grass transition temperature (Tg) of the sample through 150 minutes, then the sample is maintained at the temperature for 30 minutes; thereafter the sample is allowed to cool to the ambient temperature, and removed outside the furnace. After polishing the opposing two sides of the test piece into 10 mm thick, the glass sample is observed visually.

The expression “free from devitrification within the glass body” in this test means that the processes of heating and softening the cut and/or polished gobs or glass blocks then press-molding by use of a mold having a highly precise surface and/or the process of reheat-press processing may be easily carried out, which is an important property for the present invention. In the case of reheat-press processing, the higher is the temperature set at the reheating test, the lower is the glass viscosity, thus the pressing pressure may be reduced. However, the durability tends to be deteriorated remarkably for the press-molded products, therefore, the evaluation is preferably carried out under the condition that the preset temperature is controlled at 50 to 200 degrees C. higher than the glass transition temperature and the duration of keeping at the temperature is 5 minutes to 1 hour. More preferably, the evaluation is carried out under the condition that the preset temperature is controlled at 70 to 180 degrees C. higher than the glass transition temperature and the duration of keeping at the temperature is 10 to 40 minutes.

In addition, such a property is necessary for achieving production of optical elements with lower cost and proper productivity, such that at least one of the characteristics of there being substantially no opacification and being devitrified exists in the glass body even after certain conditions of reheating test (a) in particular after maintaining at 100 degrees C. higher than the glass transition temperature (Tg) for 30 minutes. More preferable is that at least one of the characteristics of there being substantially no opacification and/or being devitrified exists in the glass body even after maintaining at 150 degrees C. higher than the glass transition temperature (Tg) for 30 minutes.

In addition, it is preferred that value, calculated by dividing the transmissivity of the test piece after the reheating test (a) by the transmissivity of the test piece before the reheating test (a) using a radiation (D ray) of wavelength 587.56 nm, is no less than 0.95, more preferably no less than 0.96 and most preferably no less than 0.97. Furthermore, it is preferred that the difference of the wavelength λ₇₀ of the test piece before the reheating test (a) and the wavelength λ₇₀ after the reheating test (a) is no more than 20 nm, more preferably no more than 18 nm and most preferably no more than 16 nm.

The reheating test (b) is carried out in a way that a two side-polished test piece of 10 mm thick is heated from room temperature to the yield point at a rising rate of 6.5 degrees C. per second under non-oxidizing atmosphere, then is maintained at the yield point for 300 seconds, and the temperature is lowered to 220 degrees C. at a rate of 2.4 degrees C. per second, thereafter the transmissivity of the test piece of 10 mm thick is measured in the thickness direction to determine the transmissivities of before and after the test.

In the present invention, “transmissivity loss” is employed as an index for transmissivity degradation under the reheating test (b). The “transmissivity loss” corresponds to the value expressed by percentage of the difference of transmissivities measured at an identical wavelength within visible irradiation of 360 to 800 nm at which the transmissivities display the highest difference between before and after the reheating test (b). That is to say, transmissivity curves are prepared at visible wavelengths and compared for the samples before and after the reheating test (b), then the highest difference (%) of transmissivities at certain wavelength×nm is defined as the “transmissivity loss”. In the present invention, the transmissivity loss is preferably no more than 5%, more preferably no more than 4% and most preferably no more than 3%.

In the present invention, “chemical durability”, in particular water resistance is considered to represent an intimate relation with the transmissivity degradation in the reheating test. The glasses according to the present invention represent weight loss, measured by “In terms of a Chemical Durability of Optical Glass” JOGIS06-1996 specified by Japanese Optical Glass Industrial Standards, of preferably no more than 0.2% by weight, more preferably no more than 0.19% by weight and most preferably no more than 0.18% by weight.

The optical glasses of the present invention may be typically utilized for lenses, prisms and mirrors. In addition, the method of producing optical elements according to the present invention typically produces a spherical preform by flowing dropwise a melted glass from an outlet of outflow pipe formed of platinum and the like. The preform is subjected to a precision press-molding process to produce an optical element having an intended shape.

EXAMPLES

The present invention will be explained in more detail with reference to Examples and Comparative Examples, but the present invention will not be limited the Examples.

Each of a total amount of 400 g was weighed according to the compositions shown in Tables 1 to 6 as raw materials and was mixed uniformly. Each of the raw materials was melted at 950 to 1050 degrees C. for 2 to 3 hours using a quartz or platinum crucible, then the temperature was lowered to 800 to 900 degrees C. and the material was maintained additionally at the temperature for about 1 hour followed by casting into a mold to produce the respective glasses. The glass properties of the resulting glasses are shown in Tables 1 to 6. The glasses of Comparative Examples 1 and 2 having composition shown in Table 7 were also produced using the same processes with those of Examples.

The optical glasses of Examples were determined for refractive index (n_(d)), Abbe number (ν_(d)) and glass transition temperature (Tg), and the glasses were subjected to the reheating test.

The refractive index (n_(d)) and Abbe number (ν_(d)) were determined for the resulting glasses with controlling the slow-cooling temperature-dropping rate at minus 25 degrees C./hr.

The glass transition temperature (Tg) was determined using a thermodilatometer with controlling the temperature-rising rate at 8 degrees C./min.

In the reheating test (a), a test piece of 15 mm by 15 mm by 30 mm was disposed on a concave refractory and inserted into an electric heater then was reheated in a way that the temperature was raised from room temperature to a temperature of 80 degrees C. higher than the transition temperature (Tg) of each sample, i.e. the temperature at which each sample sinking into the refractory, through a period of 150 minutes. The sample was maintained at the temperature for 30 minutes then was cooled to the ambient temperature and was removed from the furnace. The opposing two sides of each sample were polished to 10 mm thick so as to observe the inside body, and the polished sample was observed visually.

The transmissivity was measured in accordance with JOGIS02-2003 specified by Japanese Optical Glass Industrial Standards. In the present invention, the transmissivity was represented rather than color degree. Specifically, an article of which the opposing sides being polished in parallel to 10±0.1 mm thick was determined for the spectral transmission factor of D ray. (D ray transmissivity after reheating test (a))/(D ray transmissivity before reheating test (a)) was obtained, and the change of the maximum transmissivity was evaluated between before and after the reheating test (a).

At the same time, the identical sample was measured as to the difference between the λ₇₀ of the test piece before the reheating test (a) and the λ₇₀ of the test piece after the reheating test (a), and the difference was considered as an index of the transmissivity degradation. The λ₇₀ refers to the wavelength at which the transmissivity comes to 70% when the transmissivity being measured at various wavelengths in accordance with JOGIS02-2003. That is to say, the less is the difference between the λ₇₀ of the test piece before the reheating test (a) and the λ₇₀ of the test piece after the reheating test (a), the less is the transmissivity degradation at the reheating test (a).

The condition of the crystal deposition was measured in accordance with JOGIS13-1994 “Method of Determining Foreign Substance within Optical Glass” specified by Japanese Optical Glass Industrial Standards. Specifically, the test piece after the reheating test was evaluated with respect to the particle size and the number of foreign substances by use of a microscope capable of detecting and measuring at least 2 micrometers or other equipment equivalent therewith. The total cross section and total number were counted as to glasses of each 100 ml and they were rated. The 1st grade indicates the total cross section being less than 0.03 mm², the 2nd grade indicates the total cross section being from no less than 0.03 mm² to less than 0.1 mm², the 3rd grade indicates the total cross section being from no less than 0.1 mm² to less than 0.25 mm², the 4th grade indicates the total cross section being from no less than 0.25 mm² to less than 0.5 mm² and the 5th grade indicates the total cross section being no less than 0.5 mm² in a glass of 100 ml respectively. The A grade indicates the total number being less than 10, the B grade indicates the total number being from no less than 10 to less than 100, the C grade indicates the total number being from no less than 100 to less than 500, the D grade indicates the total number being from no less than 500 to less than 1000 and the E grade indicates the total number being no less than 1000.

The reheating test (b) was carried out in a way that a two side-polished test piece of 10 mm thick was heated from room temperature to the yield point at a rising rate of 6.5 degrees C. per second under non-oxidizing atmosphere, then was maintained at the yield point for 300 seconds, and the temperature was lowered to 220 degrees C. at a rate of 2.4 degrees C. per second, thereafter the transmissivity of the test piece was measured in the thickness direction to determine the transmissivities of before and after the test. The transmissivity degradation means that the test piece after the test shows a lower transmissivity compared to that before the test through undergoing the reheating test (b).

In the present invention, “transmissivity loss” is employed as an index for degradation of transmissivity under the reheating test (b). The “transmissivity loss” corresponds to the value expressed by percentage of the difference of transmissivities measured at an identical wavelength within visible irradiation of 360 to 800 nm at which the transmissivities display the highest difference between before and after the reheating test (b). That is to say, transmissivity curves are prepared at visible wavelengths and compared for the samples before and after the reheating test (b), then the highest difference (%) of transmissivities at certain wavelength×nm is defined as the “transmissivity loss”.

The chemical durability or water resistance was determined in accordance with “Method of Determining Chemical Durability of Optical Glass” JOGIS06-1996 specified by Japanese Optical Glass Industrial Standards. The glass weight loss means the value, expressed as % by weight, of the glass weight reduced through the chemical durability test.

One gravity gram of glass sample, fractured into 425 to 600 micrometer grit, was weighed and put into a platinum cage. The platinum cage was inserted into a quartz-glass round-bottom flask containing-pure water of pH 6.5 to 7.5, then was treated in a boiling-water bath for 60 minutes. The weight loss % of the treated glass samples was calculated and rated such that the weight loss (wt %) of less than 0.05 being class 1, the weight loss of from 0.05 to less than 0.10 being class 2, the weight loss of from 0.10 to less than 0.25 being class 3, the weight loss of from 0.25 to less than 0.60 being class 4, the weight loss of from 0.60 to less than 1.10 being class 5 and the weight loss of no less than 1.10 being class 6; the lower is the class number, more superior is the water resistance of the glass.

TABLE 1 Examples 1 2 3 4 5 6 7 8 9 SiO₂ 4.489 4.998 4.704 4.373 4.023 4.197 3.785 3.846 4.398 B₂O₃ 11.691 10.408 12.483 11.606 16.300 16.999 15.334 15.578 11.671 SiO₂ + B₂O₃ 16.180 15.406 17.187 15.979 20.323 21.196 19.119 19.424 16.069 SiO₂/B₂O₃ 0.384 0.480 0.377 0.377 0.247 0.247 0.247 0.247 0.377 Al₂O₃ Y₂O₃ La₂O₃ Gd₂O₃ Yb₂O₃ TiO₂ 2.587 2.343 2.658 0.989 ZrO₂ Nb₂O₅ 1.688 3.464 3.289 Ta₂O₅ WO₃ 0.589 1.543 1.442 ZnO MgO 0.788 1.609 CaO SrO 3.316 BaO 19.995 15.986 15.853 23.276 30.800 26.775 26.084 21.592 25.315 RO 19.995 16.774 17.462 23.276 30.800 26.775 26.084 24.908 25.315 Li₂O 0.949 1.363 0.994 0.924 2.000 3.131 1.883 1.913 0.930 Na₂O 2.952 3.231 3.299 2.684 3.085 K₂O 2.691 3.683 1.880 1.748 1.758 Rn₂O 6.592 8.277 6.173 5.356 2.000 3.131 1.883 1.913 5.773 RO + Rn₂O 26.587 25.051 23.635 28.632 32.800 29.906 27.967 26.821 31.088 Sb₂O₃ 0.097 0.090 0.078 0.081 0.073 0.075 0.091 P₂O₅ Bi₂O₃ 52.368 53.737 54.880 51.021 46.800 48.817 52.841 53.681 51.310 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 56.857 58.735 59.584 55.394 50.823 53.014 56.626 57.527 55.708 (Al₂O₃ + ZrO₂ + SiO₂)/RO 0.225 0.298 0.269 0.188 0.131 0.157 0.145 0.154 0.174 n_(d) 1.848 1.848 1.847 1.848 1.825 1.816 1.853 1.854 1.828 ν_(d) 24.4 23.8 24.4 25.2 28.2 28.4 26.3 26.0 25.7 Tg (° C.) 367 385 415 416 431 423 417 425 386 Reheating crystal deposit 1A 1A 1A 1A 1A 1A 1A 1A 1A test (a) condition D ray 1 0.993 1 1.003 1 1 1 1 1 transmissivity after test/D ray transmissivity before test (%) λ₇₀ after test − before 15.5 16 test λ₇₀ (nm) Reheating transmissivity test (b) loss (%) glass weight loss (wt %)

TABLE 2 Examples 10 11 12 13 14 15 16 17 18 SiO₂ 3.805 4.316 4.246 4.501 4.650 4.568 4.378 4.593 B₂O₃ 15.429 11.049 16.651 11.265 11.944 12.340 12.572 11.618 11.735 SiO₂ + B₂O₃ 19.234 15.365 16.651 15.511 16.445 16.990 17.140 15.996 16.328 SiO₂/B₂O₃ 0.247 0.391 0.377 0.377 0.377 0.363 0.377 0.391 Al₂O₃ Y₂O₃ La₂O₃ Gd₂O₃ Yb₂O₃ TiO₂ 2.543 3.614 0.494 4.153 ZrO₂ Nb₂O₅ 3.366 3.292 Ta₂O₅ WO₃ 1.432 1.393 1.476 1.525 1.498 1.506 ZnO MgO 4.242 CaO SrO BaO 19.419 25.778 25.140 24.436 21.026 7.602 18.367 23.301 16.474 RO 19.419 25.778 25.140 24.436 21.026 11.844 18.367 23.301 16.474 Li₂O 1.892 0.912 0.923 0.951 0.983 0.965 0.925 0.971 Na₂O 3.027 3.063 3.157 3.261 3.204 3.071 3.221 K₂O 2.982 1.725 1.746 9.050 1.799 1.859 1.826 1.750 3.672 Rn₂O 4.874 5.664 5.732 9.050 5.907 6.103 5.995 5.745 7.864 RO + Rn₂O 24.293 31.441 30.872 33.486 26.933 17.947 24.362 29.046 24.338 Sb₂O₃ 0.090 0.087 0.093 0.096 0.094 0.090 0.095 P₂O₅ Bi₂O₃ 53.107 53.196 50.955 49.527 52.510 63.442 53.292 51.078 53.580 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 56.912 57.512 50.955 53.773 57.011 68.092 57.860 55.456 58.173 (Al₂O₃ + ZrO₂ + SiO₂)/RO 0.196 0.167 0.000 0.174 0.214 0.393 0.249 0.188 0.279 n_(d) 1.837 1.839 1.814 1.820 1.841 1.834 1.858 1.842 1.844 ν_(d) 26.0 25.5 26.4 25.8 24.9 24.4 24.2 25.3 23.9 Tg (° C.) 423 385 393 424 408 408 421 417 397 Reheating crystal deposit 1A 1A 1A 1A 1A 1A 1A 1A 1A test (a) condition D ray 1 1 1 1 1 1 1 1 1 transmissivity after test/D ray transmissivity before test (%) λ₇₀ after test − before test λ₇₀ (nm) Reheating transmissivity test (b) loss (%) glass weight loss (wt %)

TABLE 3 Examples 19 20 21 22 23 24 25 26 27 SiO₂ 4.445 4.187 4.254 4.629 4.627 4.602 4.202 3.857 3.925 B₂O₃ 11.795 11.111 8.775 12.282 12.050 11.759 11.734 15.625 15.900 SiO₂ + B₂O₃ 16.240 15.298 13.029 16.911 16.677 16.361 15.936 19.482 19.825 SiO₂/B₂O₃ 0.377 0.377 0.485 0.377 0.384 0.391 0.358 0.247 0.247 Al₂O₃ Y₂O₃ La₂O₃ Gd₂O₃ Yb₂O₃ TiO₂ 2.009 0.946 3.924 4.184 4.265 4.152 ZrO₂ Nb₂O₅ 1.671 3.149 Ta₂O₅ WO₃ 1.207 1.506 ZnO MgO 1.316 CaO SrO 8.105 BaO 22.691 20.196 20.491 17.068 17.062 16.507 16.472 21.657 22.038 RO 22.691 20.196 28.596 17.068 17.062 16.507 16.472 21.657 23.354 Li₂O 0.939 0.885 2.158 0.978 0.978 0.973 0.971 1.918 1.952 Na₂O 2.728 2.570 3.246 3.245 3.228 3.623 K₂O 1.777 1.674 3.700 3.699 3.679 3.671 3.024 Rn₂O 5.444 5.129 2.158 7.924 7.922 7.880 8.265 4.942 1.952 RO + Rn₂O 28.135 25.325 30.754 24.992 24.984 24.387 24.737 26.599 25.306 Sb₂O₃ 0.092 0.086 0.140 0.172 0.172 0.095 0.095 0.075 0.076 P₂O₅ Bi₂O₃ 51.853 55.196 56.077 54.001 53.983 53.686 53.574 53.844 54.793 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 56.298 59.383 60.330 58.630 58.610 58.288 57.776 57.701 58.718 (Al₂O₃ + ZrO₂ + SiO₂)/RO 0.196 0.207 0.149 0.271 0.271 0.279 0.255 0.178 0.168 n_(d) 1.856 1.876 1.875 1.836 1.843 1.846 1.839 1.819 1.854 ν_(d) 24.4 23.5 24.6 24.4 23.9 23.8 24.1 26.8 25.9 Tg (° C.) 404 404 405 399 397 389 397 416 409 Reheating crystal deposit 1A 1A 1A 1A 1A 1A 1A 1A 1A test (a) condition D ray 1 1 1 1 1 1 1 1 0.994 transmissivity after test/D ray transmissivity before test (%) λ₇₀ after test − before −7.5 test λ₇₀ (nm) Reheating transmissivity test (b) loss (%) glass weight loss (wt %)

TABLE 4 Examples 28 29 30 31 32 33 34 35 36 SiO₂ 3.984 4.960 4.565 4.600 4.675 4.417 4.637 4.626 4.698 B₂O₃ 16.140 13.185 12.114 12.207 10.565 11.722 11.848 11.818 10.615 SiO₂ + B₂O₃ 20.124 18.145 16.679 16.807 15.240 16.139 16.486 16.444 15.313 SiO₂/B₂O₃ 0.247 0.376 0.377 0.377 0.442 0.377 0.391 0.391 0.443 Al₂O₃ Y₂O₃ La₂O₃ Gd₂O₃ Yb₂O₃ TiO₂ 4.127 4.159 1.585 4.717 4.444 2.389 ZrO₂ Nb₂O₅ 1.758 3.322 3.533 Ta₂O₅ WO₃ 1.627 1.497 1.509 0.767 ZnO MgO 4.524 2.132 1.071 CaO SrO 6.871 BaO 12.202 11.335 18.355 16.500 15.249 23.508 16.602 17.056 13.247 RO 19.073 15.859 18.355 16.500 17.381 23.508 16.602 17.056 14.318 Li₂O 1.982 1.048 0.965 0.972 0.988 0.934 0.980 0.978 1.787 Na₂O 3.478 3.202 3.226 3.279 2.710 3.253 3.244 3.295 K₂O 3.123 1.982 1.825 3.065 4.361 1.766 3.707 3.698 4.382 Rn₂O 5.105 6.508 5.992 7.263 8.628 5.410 7.940 7.920 9.464 RO + Rn₂O 24.178 22.367 24.347 23.763 26.009 28.918 24.543 24.976 23.782 Sb₂O₃ 0.077 0.094 0.095 0.096 0.091 0.153 0.172 0.174 P₂O₅ Bi₂O₃ 55.621 57.861 53.256 53.667 54.545 51.529 54.098 53.964 54.809 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 59.605 62.821 57.821 58.267 59.220 55.946 58.735 58.590 59.507 (Al₂O₃ + ZrO₂ + SiO₂)/RO 0.209 0.313 0.249 0.279 0.269 0.188 0.279 0.271 0.328 n_(d) 1.816 1.824 1.867 1.848 1.828 1.848 1.856 1.856 1.839 ν_(d) 27.0 24.8 23.8 24 24.3 24.9 23.2 23.2 23.9 Tg (° C.) 419 393 421 409 385 395 397 395 381 Reheating crystal deposit 1A 1A 1A 1A 1A 1A 1A 1A 1A test (a) condition D ray 1 1 0.981 1 1 1 1 1 1.007 transmissivity after test/D ray transmissivity before test (%) λ₇₀ after test − before 6 15 test λ₇₀ (nm) Reheating transmissivity test (b) loss (%) glass weight loss (wt %)

TABLE 5 Examples 37 38 39 40 41 42 43 44 45 SiO₂ 4.477 4.463 4.504 4.503 4.603 4.615 4.518 4.445 4.433 B₂O₃ 11.905 8.328 10.179 10.176 11.762 11.790 11.567 8.294 10.016 SiO₂ + B₂O₃ 16.382 12.791 14.683 14.679 16.365 16.405 16.085 12.739 14.449 SiO₂/B₂O₃ 0.376 0.536 0.442 0.443 0.391 0.391 0.391 0.536 0.443 Al₂O₃ Y₂O₃ La₂O₃ Gd₂O₃ Yb₂O₃ TiO₂ 2.522 3.309 3.308 3.902 4.172 5.107 2.512 3.256 ZrO₂ Nb₂O₅ Ta₂O₅ WO₃ 1.468 1.464 1.477 1.477 1.458 1.454 ZnO MgO 4.085 CaO SrO BaO 25.727 20.850 19.576 18.778 17.973 17.516 17.187 20.766 18.466 RO 29.811 20.850 19.576 18.778 17.973 17.516 17.187 20.766 18.466 Li₂O 0.943 0.952 0.952 0.973 0.975 0.955 0.939 0.937 Na₂O 3.913 3.159 3.158 3.229 3.237 3.169 3.118 3.109 K₂O 5.352 4.201 4.600 3.680 3.689 1.806 6.515 4.134 Rn₂O 10.208 8.312 8.710 7.882 7.901 5.930 10.572 8.180 RO + Rn₂O 29.811 31.058 27.888 27.488 25.855 25.417 23.117 31.338 26.646 Sb₂O₃ 0.092 0.092 0.093 0.117 0.171 0.171 0.092 0.146 P₂O₅ Bi₂O₃ 52.242 52.072 52.550 52.931 53.706 53.835 55.691 51.861 54.049 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 56.719 56.535 57.054 57.434 58.309 58.450 60.209 56.306 58.482 (Al₂O₃ + ZrO₂ + SiO₂)/RO 0.150 0.214 0.230 0.240 0.256 0.263 0.263 0.214 0.240 n_(d) 1.867 1.829 1.829 1.835 1.840 1.845 1.880 1.842 1.853 ν_(d) 25.4 24.3 24.2 24.2 24.2 23.8 22.8 23.9 23.2 Tg (° C.) 416 379 394 405 405 389 426 374 372 Reheating crystal deposit 1A 1A 1A 1A 1A 1A 1A 1A 1A test (a) condition D ray 1 1 1 1 1 1 1 0.977 1.007 transmissivity after test/D ray transmissivity before test (%) λ₇₀ after test − before −1.5 8 test λ₇₀ (nm) Reheating transmissivity test (b) loss (%) glass weight loss (wt %)

TABLE 6 Examples 46 47 48 49 50 51 52 53 54 SiO₂ 4.467 2.954 4.025 3.900 2.460 4.315 4.353 4.476 2.849 B₂O₃ 10.093 8.900 7.772 7.530 7.127 8.666 8.743 8.989 9.904 SiO₂ + B₂O₃ 14.560 11.854 11.797 11.430 9.587 12.981 13.096 13.465 12.753 SiO₂/B₂O₃ 0.443 0.332 0.518 0.518 0.345 0.498 0.498 0.498 0.288 Al₂O₃ Y₂O₃ La₂O₃ 6.408 3.119 Gd₂O₃ 3.502 Yb₂O₃ TiO₂ 3.282 0.794 ZrO₂ 0.590 Nb₂O₅ Ta₂O₅ WO₃ 1.465 ZnO 4.001 3.634 3.320 3.117 3.931 4.041 1.930 MgO CaO SrO 1.502 1.544 1.474 BaO 18.991 7.539 6.635 2.936 5.090 RO 18.991 11.540 3.634 6.635 3.320 6.053 5.433 5.585 8.494 Li₂O 0.944 1.469 1.334 1.293 1.224 1.431 1.443 1.484 1.417 Na₂O 3.133 K₂O 4.166 Rn₂O 8.243 1.469 1.334 1.293 1.224 1.431 1.443 1.484 1.417 RO + Rn₂O 27.234 13.009 4.968 7.928 4.544 7.484 6.876 7.069 9.911 Sb₂O₃ 0.166 P₂O₅ Bi₂O₃ 53.293 68.729 83.234 80.643 85.866 75.821 76.526 78.673 77.336 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 57.76 71.683 87.259 84.543 88.326 80.726 80.879 83.149 80.185 (Al₂O₃ + ZrO₂ + SiO₂)/RO 0.235 0.256 1.108 0.588 0.741 0.810 0.801 0.801 0.335 n_(d) 1.848 1.969 2.062 2.032 1.848 2.031 2.034 2.043 2.007 ν_(d) 23.5 21.6 18.3 18.9 23.5 19.4 19.2 18.7 19.6 Tg (° C.) 395 415 388 392 395 388 385 383 380 Reheating crystal deposit 1A 1A 1A 1A 1A 1A 1A 1A 1A test (a) condition D ray 1 1 1 1 1 1 1 1 1 transmissivity after test/D ray transmissivity before test (%) λ₇₀ after test − before test λ₇₀ (nm) Reheating transmissivity test (b) loss (%) glass weight loss (wt %)

TABLE 7 Examples Comparative Examples 55 56 57 58 59 60 1 2 3 SiO₂ 5.856 5.861 5.861 4.82 4.860 5.032 4.883 4.37 B₂O₃ 13.226 12.236 13.236 12.78 12.922 15.335 26.000 12.981 11.61 SiO₂ + B₂O₃ 19.082 18.097 19.097 17.60 17.782 20.367 26.000 17.864 15.979 SiO₂/B₂O₃ 0.443 0.479 0.443 0.377 0.376 0.328 0.000 0.376 0.376 Al₂O₃ 5.538 5.542 6.542 10.000 Y₂O₃ La₂O₃ 10.000 Gd₂O₃ Yb₂O₃ TiO₂ 1.09 0.99 ZrO₂ 0.999 2.000 Nb₂O₅ 3.62 3.672 3.29 Ta₂O₅ WO₃ 1.594 1.601 ZnO 6.098 4.000 MgO 4.434 4.454 CaO 11.27 11.279 4.203 SrO 10.97 BaO 8.994 9.40 17.434 6.035 9.041 23.28 RO 11.27 11.279 8.994 20.374 21.868 16.336 4.000 13.495 23.276 Li₂O 1.02 2.054 1.063 1.032 0.92 Na₂O 3.529 3.424 2.68 K₂O 1.952 1.748 Rn₂O 0 0 0 1.02 2.05 4.59 6.408 5.356 RO + Rn₂O 11.27 11.279 0 21.394 23.918 20.926 4.000 19.903 32.632 Sb₂O₃ 0.16 0.082 0.082 0.1 0.09 P₂O₅ Bi₂O₃ 62.95 63.000 65.285 56.2 56.702 58.705 50.000 56.960 51.02 GeO₂ F TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Al₂O₃ + ZrO₂ + SiO₂ + Bi₂O₃ 75.344 76.403 77.688 61.020 61.562 63.737 60.000 61.843 55.390 (Al₂O₃ + ZrO₂ + SiO₂)/RO 1.100 1.188 1.379 0.237 0.222 0.308 2.500 0.362 0.188 n_(d) 1.855 1.86 1.856 1.913 1.866 1.836 1.748 1.847 1.857 ν_(d) 25.6 25.4 24.5 23.4 25 25.6 32.8 23.7 24.5 Tg (° C.) 492 503 458 453 519 439 415 Reheating crystal deposit 1A 1A 1A 1A 1A 1A no data non- 1A test (a) condition due to detectable higher due Tg to opacifi D ray 1 1 1 0.995 1.008 1.002 no data 0 1 transmissivity due to after test/D ray higher transmissivity Tg before test (%) λ₇₀ after test − before −13.5 16 15.5 test λ₇₀ (nm) Reheating transmissivity 1 0.7 0.9 22.27 test (b) loss (%) glass weight 0.03 0.02 0.02 0.36 loss (wt %)

The inventive glasses of Examples 1 to 57 exhibited lower glass transition temperatures compared to the glasses of Comparative Examples 1 and 2, displayed almost no crystal deposition, and were colorless and transparent, and also showed almost no change in the maximum transmissivity even after the reheating test. Furthermore, the glasses of Examples 55 to 57 represented the values of Al₂O₃+ZrO₂+SiO₂+Bi₂O₃ and (Al₂O₃+ZrO₂+SiO₂)/RO higher than a certain level, and exhibited better results in terms of reheating tests (a) and (b) compared to the glass of Comparative Example 3.

While preferred embodiments of the present invention have been described and illustrated above, it is to be understood that they are exemplary of the invention and are not to be considered to be limiting. Additions, omissions, substitutions, and other modifications can be made thereto without departing from the spirit or scope of the present invention. Accordingly, the invention is not to be considered to be limited by the foregoing description and is only limited by the scope of the appended claims. 

1. An optical glass, comprising: a refractive index (n_(d)) of no less than 1.75 and an Abbe number (ν_(d)) of no less than 10 as optical constants, wherein a Bi₂O₃ content is no less than 10% by weight to no more than 85% by weight, the ratio of SiO₂ to B₂O₃ is no more than 0.536, the total content of SiO₂+B₂O₃ is from no less than 1% by weight to no more than 60% by weight, the content of WO₃ is no more than 5% by weight, being free of Ce component, the content of Li₂O being no less than 1.293% by weight, and the optical glass has at least one of the properties of being substantially free from opacification and/or being substantially devitrified within the glass body under the conditions of the following reheating test (a), whereby, a test piece of 15 mm by 15 mm by 30 mm is reheated, such that the test piece is heated from room temperature to a temperature of 80 degrees C. higher than its transition temperature (Tg) for a period of 150 minutes, maintained for 30 minutes at the temperature of 80 degrees C. higher than the glass transition temperature (Tg) of the optical glass, allowed to cool to an ambient temperature, and finally observed visually after polishing the opposing two sides of the test piece to a thickness of 10 mm.
 2. The optical glass according to claim 1, wherein the transmissivity loss is no more than 5% at respective wavelengths in the visible region under the conditions of the following reheating test (b), wherein a two sided-polished test piece having a thickness of 10 mm is heated from room temperature to a yield point by increasing the temperature at a rate of 6.5 degrees C. per second under a non-oxidizing atmosphere, being maintained at the yield point for 300 seconds, lowering the temperature to 220 degrees C. by decreasing the temperature at a rate of 2.4 degrees C. per second, and thereafter measuring the transmissivity of the test piece to determine the transmissivity before and after the test.
 3. The optical glass according to claim 1, wherein a value, calculated by dividing the transmissivity of the test piece after the reheating test (a) by the transmissivity of the test piece before the reheating test, using a radiation (D ray) at a wavelength of 587.56 nm, is no less than 0.95.
 4. The optical glass according to claim 1, wherein the difference in a wavelength λ₇₀ of the test piece before the reheating test (a) and a wavelength λ₇₀ after the reheating test is no more than 20 nm, in which the “λ₇₀” refers to the wavelength at which the transmissivity is 70%.
 5. The optical glass according to claim 1, wherein the crystal deposit condition of the test piece after the reheating test (a) displays an internal quality of a first or second grade and A or B grade by an evaluation which is in accordance with a measuring method for inclusion JOGIS13-1994.
 6. The optical glass according to claim 1, wherein the transition temperature (Tg) of the glass is no more than 550 degrees C.
 7. The optical glass according to claim 1, wherein the total content of TiO₂+Nb₂O₅+WO₃+RO+Rn₂O is no more than 60% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; and Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.
 8. The optical glass according to claim 1, wherein the total content of TiO₂+Nb₂O₅+WO₃+RO+Rn₂O is no more than 55% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; and Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.
 9. The optical glass according to claim 1, wherein the total content of RO+Rn₂O is no more than 60% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; and Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.
 10. The optical glass according to claim 1, wherein the total content of Ln₂O₃+RO+Rn₂O is no more than 50% by weight, in which R represents one or more elements selected from the group consisting of Zn, Ba, Sr, Ca and Mg; Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs; and Ln represents one or more elements selected from the group consisting of La, Gd, Y, Ce, Eu, Dy, Yb and Lu.
 11. The optical glass according to claim 1, wherein the content of MgO is less than 4% by weight, and the content of TiO₂+Nb₂O₅+WO₃+Ln₂O₃ is no more than 10% by weight, in which Ln represents one or more elements selected from the group consisting of La, Gd, Y, Ce, Eu, Dy, Yb and Lu.
 12. The optical glass according to claim 1, wherein the content of Rn₂O is no more than 1.5% by weight, in which Rn represents one or more elements selected from the group consisting of Li, Na, K and Cs.
 13. The optical glass according to claim 1, wherein the total content of Bi₂O₃+SiO₂+Al₂O₃+ZrO₂ is no less than 75% by weight.
 14. The optical glass according to claim 1, wherein the weight loss of the glass is no more than 0.2% by weight in terms of a chemical durability test based on a powder method in accordance with JOGIS06-1996.
 15. The optical glass according to claim 1, wherein a value of (SiO₂+Al₂O₃+ZrO₂)/RO is no less than 0.5.
 16. An optical element formed by precision press-molding of the optical glass according to claim
 1. 17. A preform utilized for precision press-molding comprising of the optical glass according to claim
 1. 18. An optical element formed by precision press-molding of the preform utilized for precision press-molding according to claim
 17. 19. The optical glass according to claim 1, wherein the content of ZnO is less than 10% by weight. 